Expanded Glass for Thermal and Acoustic Insulation from Recycled Post-Consumer Glass and Textile Industry Process Waste

The production of glass foams obtained by recycling post-consumer glass and textile industry processing waste is presented. The mechanical, thermal and acoustic properties were characterized as a function of process temperature and time. The results showed that it is possible to produce glass foams with thermal and acoustic insulation properties from a mixture consisting of 96.5% of glass waste, 1% of textile waste and 2.5% of manganese dioxide, processed at temperatures between 800 and 900 °C for a time between 30 and 90 min. The samples had density in the range of 200–300 kg m−3, porosity of 87–92%, thermal conductivity of 85–105 mW m−1 K−1, noise-reducing factors of 0.15–0.40 and compressive strength of 1.2–3.0 MPa. Although their insulation performance was not as outstanding as that of polymer foams, these materials can emerge as competitive candidates for applications requiring non-flammability and high-temperature load bearing capacity in combination with low weight, mechanical strength, and thermal and acoustic insulation properties. The use of secondary raw materials (which accounted for 97.5% by weight of the synthetic blend) limits the energy required compared to that needed for the extraction, transportation and processing of primary raw materials, making these foams attractive also in terms of environmental footprint.


Introduction
The thermal comfort of enclosed spaces by heating, ventilation and air conditioning represents today 40% of energy consumption and 36% of carbon emissions in the European Union, making it one of the most energy-intensive commodity [1]. Similar values are also reported for the United States and the rest of the world [2,3]. Improved energy efficiency and proper building insulation are therefore critical to reduce the energy use, thus helping to reduce emissions associated with the combustion of fossil fuels [4,5]. Improving building thermal insulation would be also in line with the requirements of the European Commission's energy performance of building directive [6]. Theoretically, the best thermal insulation is provided by vacuum; however, a more practical solution is the use of gases (such as air), which also show very low thermal conductivities (25-26 mW m −1 K −1 ) compared to liquids and solids [7]. To further increase the thermal insulation effect of gases, their volume can be divided into small cells, which cannot effectively transfer heat by natural convection. To achieve this, an artificial material can be shaped in a cellular foam of fibrous structures to trap and/or divide different gas volumes [8]. Nowadays, the insulation materials market is dominated by inorganic fibrous materials such as glass and mineral wool (GW, MW) and organic foamy materials such as expanded or extruded polystyrene (EPS) and foamed polyurethane (PU) [4,9,10]. These traditional insulators are produced from primary raw sources, such as minerals and fossil fuels. The use of secondary or renewable raw materials is now of critical concern to meet ecological and sustainability leaves [34,35]. Some authors showed the possibility to use calcium sulfate from the ceramic industry waste [36], silicon carbide [37][38][39] and silicon nitride [40]. In this research work, we show and discuss the production of foamed glass starting from a mixture composed of 97.5% of secondary raw materials (96.5% post-consumer glass waste and 1% process waste from the synthetic textile industry) and only 2.5% of primary raw materials (manganese IV oxide, MnO 2 ). The mechanical, thermal and acoustic properties were characterized as a function of production parameters (temperature and time). Differently from other works, the commingled glass originated from municipal waste collection rather than from a specific type of glass (i.e., windows, panels, CRT screens, etc.) and was not sorted by type, composition or color. Synthetic textile process waste was used as the carbon-based pore-forming agent, while MnO 2 was used as the oxidant. The use of secondary raw materials avoids the landfilling of glass and allows also the recycling of industrial waste as a valuable and inexpensive carbon source. Thanks to its good properties and its fabrication process based on a circular economy approach, this material could be appealing for thermal and acoustic insulating applications in building and industrial applications also in terms of environmental footprint [41].

Foam Production
Manganese IV oxide (MnO 2 , reagent-grade, micrometric size) from Carlo Erba Reagents was used as purchased. Mixed glass from post-consumer items (bottles, food containers, etc.) was obtained from municipal glass waste sorting. The glass was washed and then reduced to a granulate by jaw crushers and cylindrical mills (SAIMA -Speciali Apparecchiature Industriali Meccaniche e Affini, Milano, Italy), obtaining a material with particle size between 1.5 and 2.8 mm by sieving. Glass density was determined with a Gay-Lussac pycnometer.
The chemical analysis of the glass was performed by a portable X-Ray Fluorescence (pXRF) instrument (Olympus Vanta C Series, Evident Scientific, Waltham, MA, USA) with a 4 W Ag anode X-ray tube, a silicon drift detector (SDD) and an excitation source ranging from 8 to 50 keV.
The industrial process waste (in the form of sludge) was obtained from a synthetic textile production plant. This process waste was dried at 110-120 • C for 24 h and pulverized to obtain a fine powder. This powder was characterized by means of Fourier transform infrared spectroscopy (FT-IR) with a Thermo-Nicolet Nexus 470 spectrometer, equipped with a diamond crystal attenuated total reflection (ATR) accessory. The spectra were acquired at a resolution of 2 cm −1 over a spectral range from 600 to 4000 cm −1 .
The foaming mixture was prepared by blending 96.5% wt. of glass granulate, 1% wt. of dried textile waste powder and 2.5% wt. of MnO 2 . This mixture was pulverized with a Herzog mill for 70 s, obtaining a fine powder (D 50 and D 90 particle sizes in the range of 18-20 µm and 85-95 µm, respectively). The granulometric curves were determined by light scattering techniques with a Malvern Mastersizer 2000E analyzer. The mixture (125 g) was inserted in a square steel mold (80 × 80 mm 2 ); it was first leveled manually (slight compression with the top of the mold) and then pressed by applying a 255 kN load for three minutes with a Weber PW40 hydraulic press. A green of 80 × 80 × 11 mm 3 was obtained. The green was heated (10 K min −1 ) in a FALC FM13 muffle, at different temperatures (800, 850, 875 and 900 • C) and for different times (30,45 and 90 min). After the scheduled sintering time, the samples were quickly extracted from the furnace for rapid cooling (down to 550 • C-600 • C) and then were cooled slowly in hot air for 2-3 h down to room temperature inside the furnace, which was meanwhile turned off. Rapid cooling was necessary to freeze the expanded structure, causing the viscosity of the glass to increase suddenly, while the subsequent slow cooling prevented the breakage of the specimens due to thermal contraction stresses. The samples were named after the process temperature and time (i.e.,: sample "800_30": sintered at 800 • C for 30 min; sample "850_45": 850 • C for 45 min, and so on).

Samples Dimension, Mass and Density
The sintered samples were cut into regular geometrical shapes (square-based or cylindrical). The dimensions were measured with a digital caliper (RS pro, code 841-25), rounding the value to 10 −1 mm (average of three measurements for each dimension). The mass was determined with a digital balance (Sartorius CP244S), rounding the value to 10 −1 g, while the volume was calculated as the product of the three dimensions (in the case of the square-based samples) or according to πR 2 H (with R being the radius, and H the height) for the cylindrical samples. The density of the samples (rounded value to kg m −3 ) was calculated by dividing their mass by their volume.

Porosity Characterization
A volume of 15 × 15 × 15 mm 3 was extracted from the center of each representative sample and characterized by X-ray microcomputed tomography (µCT). The acquisitions were performed by means of a custom-made cone-beam system (TOMOLAB, Elettra-Sincrotrone Trieste), with resolution of 8 µm, beam energy of 40 kV and intensity of 200 µA, with an exposure time of 2.5 s. Three-dimensional slices were reconstructed and processed with FIJI package of ImageJ2 software.

Mechanical Tests
The compression tests were performed using a Shimadzu AGS-X 10 dynamometer (10 kN load cell). The test speed was set to 1.5 mm min −1 , while the signal acquisition time was set to 0.25 s. The mechanical properties (compression modulus E and maximum strength σ M ) were determined according to ASTM C165, procedure "A" [42]. The compression toughness was determined as the area under the stress-strain curve. Each data point represents the average of five specimens.

Sound Absorption Properties
A two-microphone plane wave impedance tube (Kundt's tube) was used to determine the sound absorption properties of the samples, according to the ISO 10534-2 standard [43]. Three cylindrical samples (diameter 44 mm; thickness 18 mm) were tested for each sintering condition.

Thermal Conductivity
Thermal conductivity was measured with a Netzsch HFM 446 heat flow meter on the square-based samples (100 × 100 × 18 mm 3 ) according to the technical standard ASTM C518 [44], at an average temperature of 25 • C. Three samples were tested for each sintering condition.

Characterization of the Raw Materials
The measured density of the glass powder was 2510 ± 7 kg m −3 . The chemical analysis of the glass powder is reported in Table S1 of Supplementary Material; the grain size distribution curves and some percentiles of the mixture powder are reported in Figure S1 and Table S2 of Supplementary Materials. The FT-IR spectrum of industrial textile waste is reported in Figure S2 of Supplementary Material. The industrial textile waste was identified as a terephthalic acid salt [45], a typical monomer in the production of aromatic polyesters such as polyethylene terephthalate (PET), frequently utilized in the synthetic textile industry.

Sample Production
The combination of a carbon-based foaming agent and an oxidant reagent has already proven to be an effective way to produce low-density foamed glass [27,46]. In our work, we used organic molecules derived from industrial synthetic textile production waste, with the addition of MnO 2 . Organic molecules oxidize quickly in the presence of air at high temperatures (800-900 • C); nevertheless, these carbon-containing compounds were exposed to air only on the surface of the foaming mixture. The organic molecules inside the mixture were insulated from the air by the soften glass, and, since carbon oxidation requires a suitable amount of oxygen, they most likely underwent pyrolysis and carbonization. It was already shown that manganese IV oxide (MnO 2 ) acts both as a foaming agent and as an oxidant, since it thermally decomposes at lower oxidation states releasing oxygen gas, which can contribute to the foaming process and also oxidize carbon molecules [27]. The decomposition of MnO 2 happens in two steps: first, around 600 • C, it reduces to manganese III oxide (Mn 2 O 3 ); then, around 900-950 • C, it further reduces to manganese II oxide (MnO) [47]. The carbon molecules react with oxygen, thus releasing CO 2 gas, which acts as a foaming agent. Due to the gas production, pores emerge inside the softened glass mixture, providing a porous structure.

Sample Properties
Upon visual inspection, the overall structure of the material appeared as a foam of glass, with thin walls separating macroscopic pores. Representative pictures of the samples and their porosity are reported in Figures S3 and S4 in Supplementary Materials. Representative slices of samples from the µ-CT scans are shown in Figure 1; Figure 2 shows two representative 3D-reconstructed volumes from the µ-CT analysis (additional macrographs, micrographs and 3D volume models of all the samples are available on request). It can be seen that, additionally to the primary macro porosity, smaller secondary pores were found within the cell walls.
work, we used organic molecules derived from industrial synthetic textile production waste, with the addition of MnO2. Organic molecules oxidize quickly in the presence o air at high temperatures (800-900 °C); nevertheless, these carbon-containing compound were exposed to air only on the surface of the foaming mixture. The organic molecule inside the mixture were insulated from the air by the soften glass, and, since carbon oxi dation requires a suitable amount of oxygen, they most likely underwent pyrolysis and carbonization. It was already shown that manganese IV oxide (MnO2) acts both as a foam ing agent and as an oxidant, since it thermally decomposes at lower oxidation states re leasing oxygen gas, which can contribute to the foaming process and also oxidize carbon molecules [27]. The decomposition of MnO2 happens in two steps: first, around 600 °C, i reduces to manganese III oxide (Mn2O3); then, around 900-950 °C, it further reduces to manganese II oxide (MnO) [47]. The carbon molecules react with oxygen, thus releasing CO2 gas, which acts as a foaming agent. Due to the gas production, pores emerge inside the softened glass mixture, providing a porous structure.

Sample Properties
Upon visual inspection, the overall structure of the material appeared as a foam o glass, with thin walls separating macroscopic pores. Representative pictures of the sam ples and their porosity are reported in Figures S3 and S4 of Supplementary information Representative slices of samples from the µ-CT scans are shown in Figure 1; Figure 2 shows two representative 3D-reconstructed volumes from the µ-CT analysis (additiona macrographs, micrographs and 3D volume models of all the samples are available on re quest). It can be seen that, additionally to the primary macro porosity, smaller secondary pores were found within the cell walls.
The samples' density, thermal conductivity, mechanical and acoustic properties are reported in Table 1.    The samples' density, thermal conductivity, mechanical and acoustic properties are reported in Table 1.

Density
The density of the samples sintered between 850 and 900 • C lay in the range of 210-230 kg m −3 , while the samples produced at 800 • C had higher densities (275-300 kg m −3 ). For comparison, rock and glass wools are lighter (100-150 kg m −3 ) than our expanded glass samples, and polymeric foams are even much lighter (15-20 kg m −3 ). Considering an average density of soda-lime glass of 2500 kg m −3 (2400-2800 kg m −3 ) [48], which is in line with the measured density of the glass powder used in this work (2510 ± 7 kg m −3 ), we assumed a porosity (as volumetric void percentage) between 88% and 91%. Similar results of porosity values were determined by µ-CT, as reported in Table 2. The density values (as seen in Figure 3) appeared to be slightly correlated with the process time, with opposite trends: the density decreased with the sintering time for samples sintered at 800 • C, while it increased modestly with the sintering time for the other samples.

Porosity
The primary and secondary pore sizes are reported in Table 2 and Figures The thickness of the cell walls is reported in Table 2. The percentage of porosity mined as the complementary of the solid volume fraction calculated after µ-CT a is also reported in Table 2. The size of the primary pores seemed to increase with tering time for samples produced at 800 °C and to slightly increase with the sinter for samples produced at 850 °C. Conversely, the size of the primary pores for produced at 875 °C and 900 °C showed the maximum value at a processing time of On the other hand, the size of the secondary pores did not seem to be influenced sintering time, but increased with the process temperature. The porosity lay in th range (85-89%) for all samples except for those produced at 800 °C for 30 min, fo the value was lower (81%). Porosity can be closed (i.e., the cells are isolated fro other) or open. In the first scenario (porosity predominantly closed), the materia good thermal insulation properties; in the second scenario (porosity predominantl the thermal insulation properties are slightly reduced, but the sound insulation c ties are improved [30,49].

Porosity
The primary and secondary pore sizes are reported in Table 2 and Figures 4 and 5. The thickness of the cell walls is reported in Table 2. The percentage of porosity, determined as the complementary of the solid volume fraction calculated after µ-CT analysis, is also reported in Table 2. The size of the primary pores seemed to increase with the sintering time for samples produced at 800 • C and to slightly increase with the sintering time for samples produced at 850 • C. Conversely, the size of the primary pores for samples produced at 875 • C and 900 • C showed the maximum value at a processing time of 45 min. On the other hand, the size of the secondary pores did not seem to be influenced by the sintering time, but increased with the process temperature. The porosity lay in the same range (85-89%) for all samples except for those produced at 800 • C for 30 min, for which the value was lower (81%). Porosity can be closed (i.e., the cells are isolated from each other) or open. In the first scenario (porosity predominantly closed), the material shows good thermal insulation properties; in the second scenario (porosity predominantly open), the thermal insulation properties are slightly reduced, but the sound insulation capabilities are improved [30,49].

Porosity
The primary and secondary pore sizes are reported in Table 2 and Figures 4 and 5 The thickness of the cell walls is reported in Table 2. The percentage of porosity, deter mined as the complementary of the solid volume fraction calculated after µ-CT analysis is also reported in Table 2. The size of the primary pores seemed to increase with the sin tering time for samples produced at 800 °C and to slightly increase with the sintering time for samples produced at 850 °C. Conversely, the size of the primary pores for samples produced at 875 °C and 900 °C showed the maximum value at a processing time of 45 min On the other hand, the size of the secondary pores did not seem to be influenced by the sintering time, but increased with the process temperature. The porosity lay in the same range (85-89%) for all samples except for those produced at 800 °C for 30 min, for which the value was lower (81%). Porosity can be closed (i.e., the cells are isolated from each other) or open. In the first scenario (porosity predominantly closed), the material shows good thermal insulation properties; in the second scenario (porosity predominantly open) the thermal insulation properties are slightly reduced, but the sound insulation capabili ties are improved [30,49].  The production of foamed glass is controlled by many factors (glass composition particle size, additives, process temperature, etc.). Once the characteristics of the glass and additives are settled, the process temperature is the key parameter that influences the foam properties, since the density and type of porosity are directly determined by the glass viscosity, the rate of bubble formation and coalescence [25,28,50]. Glass viscosity η is a function of the temperature and of the parameters A, B and T0 [48]: (1 For soda-lime glass, we assume A = −2.464, B = 3828 and T0 = 272.7 °C [48]. Therefore η = 6 × 10 4 Pa•s (800 °C), 1.4 × 10 4 Pa•s (850 °C), 7.5 × 10 3 Pa•s (875 °C) and 4.2 × 10 3 Pa•s (900 °C). It can be noticed that the glass viscosity values at 850, 875 and 900 °C are about 24% 13% and 7% of the viscosity value at 800 °C. It is also known that higher temperatures (which provide lower viscosities) lead to the rapid formation and coalescence of gas bub bles, resulting in foam collapse. From these premises, it can be assumed that the higher glass viscosity of the sample produced at 800 °C led to smaller pores and a closed-cel structure.

Mechanical Properties
The average curves of the compression tests are shown in Figure S5 of Supplemen tary Material. The values of modulus, strength and toughness determined after the com pression tests are reported in Table 1. All samples showed mechanical properties tha were superior to those of polymer foams (EPS and PU) [51][52][53][54] and outperformed by fa those of mineral-based insulation materials (glass wool and mineral wool) [55], which wil make them particularly suitable for load-bearing applications. The compressive modulus ( Figure 6 and Figure 7) increased from 30 to 45 min of sintering time, while it remained unchanged after increasing the sintering time from 45 to 90 min. This behavior was ob served for samples processed at 850 °C or higher, while the trend was the opposite for the sample at 800 °C, which showed a reduction of the compressive modulus from 30 to 45 min of sintering. The modulus then remained constant when increasing the sintering time from 45 to 90 min. This behavior can be explained by the very small pore size of the sample sintered for 30 min, when compared with the pore size of other samples at longer sintering times. This condition negatively affects the density, but enhances the mechanical strength The production of foamed glass is controlled by many factors (glass composition, particle size, additives, process temperature, etc.). Once the characteristics of the glass and additives are settled, the process temperature is the key parameter that influences the foam properties, since the density and type of porosity are directly determined by the glass viscosity, the rate of bubble formation and coalescence [25,28,50]. Glass viscosity η is a function of the temperature and of the parameters A, B and T 0 [48]: For soda-lime glass, we assume A = −2.464, B = 3828 and T 0 = 272.7 • C [48]. Therefore, η = 6 × 10 4 Pa·s (800 • C), 1.4 × 10 4 Pa·s (850 • C), 7.5 × 10 3 Pa·s (875 • C) and 4.2 × 10 3 Pa·s (900 • C). It can be noticed that the glass viscosity values at 850, 875 and 900 • C are about 24%, 13% and 7% of the viscosity value at 800 • C. It is also known that higher temperatures (which provide lower viscosities) lead to the rapid formation and coalescence of gas bubbles, resulting in foam collapse. From these premises, it can be assumed that the higher glass viscosity of the sample produced at 800 • C led to smaller pores and a closed-cell structure.

Mechanical Properties
The average curves of the compression tests are shown in Figure S5 of Supplementary Material. The values of modulus, strength and toughness determined after the compression tests are reported in Table 1. All samples showed mechanical properties that were superior to those of polymer foams (EPS and PU) [51][52][53][54] and outperformed by far those of mineralbased insulation materials (glass wool and mineral wool) [55], which will make them particularly suitable for load-bearing applications. The compressive modulus (Figures 6 and 7) increased from 30 to 45 min of sintering time, while it remained unchanged after increasing the sintering time from 45 to 90 min. This behavior was observed for samples processed at 850 • C or higher, while the trend was the opposite for the sample at 800 • C, which showed a reduction of the compressive modulus from 30 to 45 min of sintering. The modulus then remained constant when increasing the sintering time from 45 to 90 min. This behavior can be explained by the very small pore size of the sample sintered for 30 min, when compared with the pore size of other samples at longer sintering times. This condition negatively affects the density, but enhances the mechanical strength. Materials 2023, 16, x FOR PEER REVIEW 9 of 16  The best mechanical performances, in terms of strength and modulus, were recorded for the samples produced at 800 °C for 30 min. The specimens' breaking behavior was highly variable (some sample failed under a 10-15% strain, others resisted up to a 55% strain), but none of them was truly brittle (in fact, no specimen failed suddenly, as can be noticed from the curve reported in Supplementary information, Figure S5.). The overall toughness is indicated by the successive failure of individual cell structures (whose walls, made of glass, are brittle). The absorbed compressive energy (Figure 8), which can be directly related to the toughness of a sample, was higher for specimens produced at 800 °C and shorter times (22 J and 12 J, for samples sintered at 800 °C for 30 min and 45 min, respectively), while all the other samples showed an average absorbed energy between 3 and 10 J. Figure 9 and Figure 10 reports values of compressive modulus and strength as a function of density, cell wall thickness and pore size.   The best mechanical performances, in terms of strength and modulus, were recorded for the samples produced at 800 °C for 30 min. The specimens' breaking behavior was highly variable (some sample failed under a 10-15% strain, others resisted up to a 55% strain), but none of them was truly brittle (in fact, no specimen failed suddenly, as can be noticed from the curve reported in Supplementary information, Figure S5.). The overall toughness is indicated by the successive failure of individual cell structures (whose walls, made of glass, are brittle). The absorbed compressive energy (Figure 8), which can be directly related to the toughness of a sample, was higher for specimens produced at 800 °C and shorter times (22 J and 12 J, for samples sintered at 800 °C for 30 min and 45 min, respectively), while all the other samples showed an average absorbed energy between 3 and 10 J. Figure 9 and Figure 10 reports values of compressive modulus and strength as a function of density, cell wall thickness and pore size.  The best mechanical performances, in terms of strength and modulus, were recorded for the samples produced at 800 • C for 30 min. The specimens' breaking behavior was highly variable (some sample failed under a 10-15% strain, others resisted up to a 55% strain), but none of them was truly brittle (in fact, no specimen failed suddenly, as can be noticed from the curve reported in Supplementary Materials, Figure S5.). The overall toughness is indicated by the successive failure of individual cell structures (whose walls, made of glass, are brittle). The absorbed compressive energy (Figure 8), which can be directly related to the toughness of a sample, was higher for specimens produced at 800 • C and shorter times (22 J and 12 J, for samples sintered at 800 • C for 30 min and 45 min, respectively), while all the other samples showed an average absorbed energy between 3 and 10 J. Figures 9 and 10 reports values of compressive modulus and strength as a function of density, cell wall thickness and pore size.  The best mechanical performances, in terms of strength and modulus, were recorded for the samples produced at 800 °C for 30 min. The specimens' breaking behavior was highly variable (some sample failed under a 10-15% strain, others resisted up to a 55% strain), but none of them was truly brittle (in fact, no specimen failed suddenly, as can be noticed from the curve reported in Supplementary information, Figure S5.). The overall toughness is indicated by the successive failure of individual cell structures (whose walls, made of glass, are brittle). The absorbed compressive energy (Figure 8), which can be directly related to the toughness of a sample, was higher for specimens produced at 800 °C and shorter times (22 J and 12 J, for samples sintered at 800 °C for 30 min and 45 min, respectively), while all the other samples showed an average absorbed energy between 3 and 10 J. Figure 9 and Figure 10 reports values of compressive modulus and strength as a function of density, cell wall thickness and pore size.   The values of E, as expected, seemed to be loosely related to the density: heavier samples were stiffer, as seen in Figure 9a. However, the relation is more complex, since  The values of E, as expected, seemed to be loosely related to the density: heavier samples were stiffer, as seen in Figure 9a. However, the relation is more complex, since The values of E, as expected, seemed to be loosely related to the density: heavier samples were stiffer, as seen in Figure 9a. However, the relation is more complex, since the type of cell structure (open or closed porosity) and the presence of secondary porosity can also influence the modulus. From the Gibson-Ashby model [56][57][58], the elastic modulus of the cellular material can be related to the density and the type of porosity: where E is the elastic modulus of the cellular material, E 0 is the elastic modulus of the bulk material (for the average soda-lime glass, 70 GPa [48]), ρ is the density of the foam, and ρ 0 is the density of the glass (2500 kg m −3 [48]). ϕ is a parameter defined as the ratio of the volume of material on the faces to that on the edges. For an open-cell material, ϕ = 0; for a closed-cell material, ϕ = l/t, where l is the length of the array members of the cell, and t is their thickness. In practical terms, the material behaves as an open-cell foam when ϕ < 1, and as a closed-cell foam when ϕ > 5. From the experimentally determined moduli, it was possible to derive the value of ϕ for each sample, inferring the type of porosity (open or close), as reported in Table 3, where E 1 * (ϕ = 1) is the theoretical value of E, calculated with Equation (1), assuming a value of ϕ = 1 (nearly open-cell structure). E 5 * (ϕ = 5) is the theoretical value of E, calculated with Equation (1), assuming a value of ϕ = 5 (closed-cell structure). ϕ* is the value of ϕ to be input in Equation (1) to obtain a theoretical value of E equal to that obtained experimentally from the compression tests. A value of ϕ * close to 1 is an indication of an open-cell structure, while a value of ϕ * close to (or greater than) 5 suggests a closed-cell structure. It is possible to notice that the samples obtained at lower temperatures (particularly those sintered at 800 • C) showed higher ϕ * values, while those obtained at higher temperatures had lower ϕ* values. Moreover, longer process times seemed to result in lower ϕ* values (favoring an open-cell structure). As discussed earlier, the mechanical properties were quite similar for samples produced at 850, 875 and 900 • C, while they were superior for samples produced at 800 • C (with the best performances recorded for samples produced at 800 • C for 30 min). This can be explained by their higher density and the prevalence of a closed-cell structure, deduced from the ϕ* values calculated above (Table 3).

Thermal Insulation Properties
The thermal conductivity (λ, reported in Table 1) ranged from 86 to 104 mW m −1 K −1 . It appeared to be only loosely related to the density of the samples (with heavier samples showing higher conductivity, as seen in Figure 11). At all process temperatures, the thermal conductivity values seemed to increase moderately with the sintering time (the samples foamed for 90 min showed the highest conductivity, as seen in Figure 12). showing higher conductivity, as seen in Figure 11). At all process temperatures, the thermal conductivity values seemed to increase moderately with the sintering time (the samples foamed for 90 min showed the highest conductivity, as seen in Figure 12). Figure 11. Thermal conductivity as a function of density. For comparison, rock wool, glass wool, expanded polystyrene or polyurethane foam perform better: their values of thermal conductivity, ranging from 20 to 30 mW m −1 K −1 [4,51,52,59], are about from 1/3 to 1/5 of those registered for our expanded glasses. The thermal conductivity should be affected by density and porosity type, with a closed-cell structure favoring thermal insulation. Thermal conduction in the solid phase, related to the density of a sample, contributes to most of the overall thermal conductivity, while conduction in the gas phase is greater in an open-cell structure, due to the different gas composition (air instead of CO2) and to the possible convective heat transfer [7,49].

Acoustic Properties
The average sound absorption coefficient curves as a function of sound frequency are reported in Figure 13; the noise reduction coefficient (NRC) values are reported in Table  1. It can be noticed that all samples has a low sound absorption at low frequencies. As the sound frequency increased, the absorption coefficient rose until it reached a value of 0.5 above 800 Hz. As the frequency increase further, the coefficient remained high, particularly in the range of the frequencies best heard by the human ear, indicated between 2000 and 5000 Hz. For the samples sintered at 800 °C, the absorption properties were worse compared to the other samples, and the absorption maximum was located at higher frequencies (1600-2000 Hz). The samples produced at 850-900 °C appeared to have a very showing higher conductivity, as seen in Figure 11). At all process temperatures, the thermal conductivity values seemed to increase moderately with the sintering time (the samples foamed for 90 min showed the highest conductivity, as seen in Figure 12). Figure 11. Thermal conductivity as a function of density. For comparison, rock wool, glass wool, expanded polystyrene or polyurethane foam perform better: their values of thermal conductivity, ranging from 20 to 30 mW m −1 K −1 [4,51,52,59], are about from 1/3 to 1/5 of those registered for our expanded glasses. The thermal conductivity should be affected by density and porosity type, with a closed-cell structure favoring thermal insulation. Thermal conduction in the solid phase, related to the density of a sample, contributes to most of the overall thermal conductivity, while conduction in the gas phase is greater in an open-cell structure, due to the different gas composition (air instead of CO2) and to the possible convective heat transfer [7,49].

Acoustic Properties
The average sound absorption coefficient curves as a function of sound frequency are reported in Figure 13; the noise reduction coefficient (NRC) values are reported in Table  1. It can be noticed that all samples has a low sound absorption at low frequencies. As the sound frequency increased, the absorption coefficient rose until it reached a value of 0.5 above 800 Hz. As the frequency increase further, the coefficient remained high, particularly in the range of the frequencies best heard by the human ear, indicated between 2000 and 5000 Hz. For the samples sintered at 800 °C, the absorption properties were worse compared to the other samples, and the absorption maximum was located at higher frequencies (1600-2000 Hz). The samples produced at 850-900 °C appeared to have a very For comparison, rock wool, glass wool, expanded polystyrene or polyurethane foam perform better: their values of thermal conductivity, ranging from 20 to 30 mW m −1 K −1 [4,51,52,59], are about from 1/3 to 1/5 of those registered for our expanded glasses. The thermal conductivity should be affected by density and porosity type, with a closed-cell structure favoring thermal insulation. Thermal conduction in the solid phase, related to the density of a sample, contributes to most of the overall thermal conductivity, while conduction in the gas phase is greater in an open-cell structure, due to the different gas composition (air instead of CO 2 ) and to the possible convective heat transfer [7,49].

Acoustic Properties
The average sound absorption coefficient curves as a function of sound frequency are reported in Figure 13; the noise reduction coefficient (NRC) values are reported in Table 1. It can be noticed that all samples has a low sound absorption at low frequencies.
As the sound frequency increased, the absorption coefficient rose until it reached a value of 0.5 above 800 Hz. As the frequency increase further, the coefficient remained high, particularly in the range of the frequencies best heard by the human ear, indicated between 2000 and 5000 Hz. For the samples sintered at 800 • C, the absorption properties were worse compared to the other samples, and the absorption maximum was located at higher frequencies (1600-2000 Hz). The samples produced at 850-900 • C appeared to have a very similar acoustic performance (apparently unrelated to processing temperature or time), while the worst performing samples (with completely different curves and behavior) seemed to be those produced at 800 • C. The acoustic performance can be related, again, to both density and porosity type (with open porosity providing better acoustic insulation performances). The closed-cell structure of the samples sintered at 800 • C was likely responsible for their poor acoustic performance. similar acoustic performance (apparently unrelated to processing temperature or time), while the worst performing samples (with completely different curves and behavior) seemed to be those produced at 800 °C. The acoustic performance can be related, again, to both density and porosity type (with open porosity providing better acoustic insulation performances). The closed-cell structure of the samples sintered at 800 °C was likely responsible for their poor acoustic performance. Figure 13. Sound absorption coefficient as a function of frequency for the different samples.

Process Parameters
The thermal and acoustic properties were significantly better for samples produced at 850, 875 and 900 °C with respect to samples produced at 800 °C. However, since there were no substantial differences between the samples produced at 850 °C for intermediate times (45 min) and those produced at 900 °C for long times (90 min), from an energysaving and optimization perspective it would be meaningless to spend energy and time (900 °C for 90 min), as the samples produced at 850 °C for 45 min already achieved satisfactory performances.
Aiming at optimizing the thermal and acoustic properties, the samples sintered at 850, 875 and 900 °C for different firing times were comparable. This implies that the production at 850 °C for 45 min was the most cost-effective one. On the other hand, if the mechanical property of compressive strength is considered, the best result was provided by the samples sintered at 800 °C for 30 min. In general, for the purpose of economic feasibility of the process, it is better to favor shorter times (higher production) than lower temperatures (energy saving).

Conclusions
The results showed that it is possible to produce glass foams from a mixture composed of 96.5% w/w of blended glass waste, 1% w/w of textile waste and 2.5% of MnO2 w/w, sintered at a temperature between 800 and 900 °C for a time between 30 and 90 min. The products had a density between 200 and 300 kg m −3 , a porosity between 81% and 90%, a thermal conductivity between 85 and 105 mW m −1 K −1 , noise-reducing factors between 0.15 and 0.4 and a compressive strength between 1.2 and 3 MPa. These materials are attractive candidates for applications that require a good combination of low weight, thermal/acoustic insulation and mechanical strength. Although the insulation performance was not outstanding when compared with that of other types of insulation materials (such as polymeric foams), in load-bearing applications where stiffness, mechanical strength, chemical inertia, non-flammability and high-temperature resistance are crucial, the glass foams investigated in this study may emerge as competitive alternatives. Moreover, in the next future, a manufacturing process able to reduce energy consumption, raw material

Process Parameters
The thermal and acoustic properties were significantly better for samples produced at 850, 875 and 900 • C with respect to samples produced at 800 • C. However, since there were no substantial differences between the samples produced at 850 • C for intermediate times (45 min) and those produced at 900 • C for long times (90 min), from an energy-saving and optimization perspective it would be meaningless to spend energy and time (900 • C for 90 min), as the samples produced at 850 • C for 45 min already achieved satisfactory performances.
Aiming at optimizing the thermal and acoustic properties, the samples sintered at 850, 875 and 900 • C for different firing times were comparable. This implies that the production at 850 • C for 45 min was the most cost-effective one. On the other hand, if the mechanical property of compressive strength is considered, the best result was provided by the samples sintered at 800 • C for 30 min. In general, for the purpose of economic feasibility of the process, it is better to favor shorter times (higher production) than lower temperatures (energy saving).

Conclusions
The results showed that it is possible to produce glass foams from a mixture composed of 96.5% w/w of blended glass waste, 1% w/w of textile waste and 2.5% of MnO 2 w/w, sintered at a temperature between 800 and 900 • C for a time between 30 and 90 min. The products had a density between 200 and 300 kg m −3 , a porosity between 81% and 90%, a thermal conductivity between 85 and 105 mW m −1 K −1 , noise-reducing factors between 0.15 and 0.4 and a compressive strength between 1.2 and 3 MPa. These materials are attractive candidates for applications that require a good combination of low weight, thermal/acoustic insulation and mechanical strength. Although the insulation performance was not outstanding when compared with that of other types of insulation materials (such as polymeric foams), in load-bearing applications where stiffness, mechanical strength, chemical inertia, non-flammability and high-temperature resistance are crucial, the glass foams investigated in this study may emerge as competitive alternatives. Moreover, in the next future, a manufacturing process able to reduce energy consumption, raw material use and CO 2 emissions will be strategic and will assume a significant value. The production method used for the samples examined in this study, starting from secondary raw materials, allows reducing the energy required compared to that needed for the extraction, transportation and processing of raw materials, with obvious benefits in terms of environmental indexes.
Supplementary Materials: The following supporting information can be downloaded at: https: //www.mdpi.com/article/10.3390/ma16041721/s1, Table S1: chemical analysis of post-consumer glass powder (secondary raw materials) by XRF; Table S2: characteristic diameters of the synthesis mixture powder from the granulometric analysis; Table S3: vibrational bands of the FTIR spectrum of textile industrial scraps; Figure S1: granulometric curve of the synthesis mixture powder; Figure S2: FTIR spectrum of textile industrial scraps; Figure S3: macrographs of the different samples; Figure S4: representative pictures of some of the produced samples, before and after cutting into the final size; Figure S5: compression stress/strain curves of different samples.